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CN104040008A - Hot stamp molded article and method for producing same - Google Patents

Hot stamp molded article and method for producing same Download PDF

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Publication number
CN104040008A
CN104040008A CN201380005178.9A CN201380005178A CN104040008A CN 104040008 A CN104040008 A CN 104040008A CN 201380005178 A CN201380005178 A CN 201380005178A CN 104040008 A CN104040008 A CN 104040008A
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CN
China
Prior art keywords
shaping body
stamping
content
heat stamping
hot
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN201380005178.9A
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Chinese (zh)
Other versions
CN104040008B (en
Inventor
野中俊树
加藤敏
川崎薰
友清寿雅
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
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Nippon Steel Corp
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Publication of CN104040008A publication Critical patent/CN104040008A/en
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Publication of CN104040008B publication Critical patent/CN104040008B/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/1275—Next to Group VIII or IB metal-base component
    • Y10T428/12757—Fe
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
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    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

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  • Chemical Kinetics & Catalysis (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

A hot stamp molded article is characterized in that when the carbon content (mass%), silicon content (mass%) and manganese content (mass%) are expressed as [C], [Si] and [Mn], respectively, a relationship of (5*[Si] + [Mn])/[C] > 10 holds, and if the metal structure contains martensite at 80% or more by area ratio, and further contains one or more of perlite at 10% or less by area ratio, retained austenite at 5% or less by volume ratio, ferrite at 20% or less by area ratio, and bainite at less than 20% by area ratio, TS lambda, which is the product of the tensile strength (TS) and hole expansion rate (lambda), is at least 50000 MPa.%, and the hardness of the martensite, as measured by a nanoindenter, satisfies H2/H1 < 1.10 and sigmaHM < 20.

Description

Heat stamping and shaping body and manufacture method thereof
Technical field
The present invention relates to use heat stamping and shaping body and the manufacture method thereof of hot stamping by the formability excellence of cold-rolled steel sheet.Cold-rolled steel sheet of the present invention comprises cold-rolled steel sheet, galvanizing cold-rolled steel sheet, alloyed hot-dip zinc-coated cold-rolled steel sheet, electrolytic zinc-coated cold-rolled steel sheet and the cold-rolled steel sheet of aluminizing.
The Japanese Patent Application of the application based on proposing in Japan on January 13rd, 2012 advocated right of priority No. 2012-004552, at this, quotes its content.
Background technology
Now, for automotive sheet, require to improve it and collide security and make its lightweight.Now, not only need to count with tensile strength the steel plate of 980MPa level (more than 980MPa), 1180MPa level (more than 1180MPa), but also need more high-intensity steel plate.The steel plate that for example, need to surpass 1.5GPa.Under such situation, as obtaining high-intensity method, enjoy recently that to gaze at be hot stamping (be also referred to as hot pressing, die quenching, push down quenching etc.).Hot stamping refers to following forming method: after steel plate is heated to 750 ℃ of above temperature, by hot rolling, carry out moulding (processing), make thus the formability of high tensile steel plate improve, quench, thereby obtain desirable material after moulding by cooling.
As with press processability and high-intensity steel plate, known have the steel plate that contains retained austenite in the steel plate that comprises ferrite-martensitic stucture, the steel plate that comprises ferrite-bainite structure or tissue etc.Wherein, make the yield ratio of the complex tissue steel plate (comprising ferrite-martensitic steel plate, so-called DP steel plate) that martensite forms in being dispersed at the bottom of ferrite base low, tensile strength is high, and tensile properties is excellent.But above-mentioned complex tissue steel plate, because stress concentration is at ferrite and martensitic interface, easily cracks thus, so there is the poor such shortcoming of hole expandability.In addition, the steel plate that has such complex tissue can not be brought into play the tensile strength of 1.5GPa level.
For example, in patent documentation 1～3, disclose complex tissue steel plate as above.In addition, in patent documentation 4～6 relevant for the record of hardness and the relation between formability of high tensile steel plate.
Yet, even if utilize these prior aries, be also difficult to tackle current the require further lightweight of automobile, the further requirement of the processing characteristicies such as hole expandability after complicated, the hot stamping of high strength, component shape.
Prior art document
Patent documentation
Patent documentation 1: Japanese kokai publication hei 6-128688 communique
Patent documentation 2: TOHKEMY 2000-319756 communique
Patent documentation 3: TOHKEMY 2005-120436 communique
Patent documentation 4: TOHKEMY 2005-256141 communique
Patent documentation 5: TOHKEMY 2001-355044 communique
Patent documentation 6: Japanese kokai publication hei 11-189842 communique
Summary of the invention
Invent problem to be solved
The present invention carries out in view of the above problems.That is, the object of the invention is to: provide guarantee that 1.5GPa is above, be preferably 1.8GPa above, more preferably intensity more than 2.0GPa and have better hole expandability use heat stamping and shaping body and the manufacture method thereof of cold-rolled steel sheet (comprising as described later the steel plate that zinc plates or aluminizes and form) hot stamping for.Here, heat stamping and shaping body refers to the above-mentioned hot stamping formed body that moulding processes by hot stamping as starting material with cold-rolled steel sheet.
For the means of dealing with problems
First inventors of the present invention guarantee for intensity that 1.5GPa is above, be preferably the hot stamping of using in 1.8GPa heat stamping and shaping body above, that more preferably 2.0GPa is above and formability (hole expandability) is excellent and conduct in-depth research by cold-rolled steel sheet and hot stamping condition.Consequently, find: by (i), for composition of steel, the relation of Si, Mn and C content is set as to suitable relation; (ii) by ferrite, martensitic minute rate (area occupation ratio) be set as regulation minute rate; (iii) adjust cold rolling draft, thereby making the thickness of slab skin section (skin section) of steel plate and the martensitic hardness ratio of thickness of slab central part (central part) (hardness poor) and the martensitic Hardness Distribution of central part is in specific scope, can in cold-rolled steel sheet for hot stamping (cold-rolled steel sheet before hot stamping), guarantee than in the past higher formability thus, that is, long-pending TS * λ of tensile strength TS and hole expansibility λ can guarantee for more than 50000MPa%.Cold-rolled steel sheet before hot stamping refer to be heated to 750 ℃～1000 ℃ and process, the cold-rolled steel sheet of the state before the heating in cooling hot stamping operation.In addition, find: if this hot stamping is carried out to hot stamping with cold-rolled steel sheet with hot stamping condition described later, even after hot stamping, the thickness of slab skin section of steel plate and the martensitic hardness of the central part when martensitic Hardness Distribution of central part are also roughly maintained, and can obtain TS * λ and be more than 50000MPa% high strength and the heat stamping and shaping body of formability excellence.In addition, also find: suppressing hot stamping is also effective with the segregation of the MnS at the thickness of slab central part place of cold-rolled steel sheet for the formability (hole expandability) that improves heat stamping and shaping body.
In addition, also find: by cold rolling from the frame of upstream to the cold rolling rate of each frame by the 3rd section of upstream number and the ratio of total cold rolling rate (accumulation rolling rate) to be set in specific scope be effective for the martensitic hardness of control.Based on above-mentioned discovery, inventors of the present invention have found each scheme of invention shown below.In addition, even if also found that hot stamping is carried out to galvanizing, alloyed hot-dip zinc-coated, electro-galvanizing and the cold-rolled steel sheet of aluminizing with cold-rolled steel sheet can not damage its effect yet.
(1), the heat stamping and shaping body of a scheme of the present invention is characterised in that, it be take quality % and contains C: surpass 0.150% and as below 0.300%, Si:0.010%～1.000%, Mn:1.50%～2.70%, P:0.001%～0.060%, S:0.001%～0.010%, N:0.0005%～0.0100% and Al:0.010%～0.050%, optionally contain B:0.0005%～0.0020% sometimes, Mo:0.01%～0.50%, Cr:0.01%～0.50%, V:0.001%～0.100%, Ti:0.001%～0.100%, Nb:0.001%～0.050%, Ni:0.01%～1.00%, Cu:0.01%～1.00%, more than one in Ca:0.0005%～0.0050% and REM:0.0005%～0.0050%, remainder comprises Fe and inevitable impurity, when by C content, Si content and Mn content be take unit and are expressed as [C] as quality %, when [Si] and [Mn], set up the relation of following formula a, metal structure contains with area occupation ratio counts more than 80% martensite, sometimes also contains with area occupation ratio and counts the perlite below 10%, with volume fraction, count the retained austenite below 5%, in area occupation ratio, count 0～20% ferrite and with area occupation ratio, be less than more than one in 20% bainite, the amassing of tensile strength TS and hole expansibility λ is that TS * λ is more than 50000MPa%, and the above-mentioned martensitic hardness recording with nano-hardness tester meets following formula b and formula c.
5×[Si]+[Mn])/[C]＞10 (a)
H2/H1＜1.10 (b)
σHM＜20 (c)
In formula, H1 is the above-mentioned martensitic average hardness of skin section, H2 is for being the above-mentioned martensitic average hardness of thickness of slab central part from thickness of slab center along the scope of thickness of slab direction ± 100 μ m, and σ HM is the dispersion value that is present in the above-mentioned martensitic hardness of above-mentioned thickness of slab central part.
(2), according to the heat stamping and shaping body above-mentioned (1) Suo Shu, wherein, the area occupation ratio that is present in diameter of equivalent circle in above-mentioned metal structure and is the MnS of 0.1 μ m～10 μ m can, for below 0.01%, be set up following formula d.
n2/n1＜1.5 (d)
In formula, n1 is every 10000 μ m of 1/4 of thickness of slab 2the mean number density of above-mentioned MnS, n2 is every 10000 μ m of above-mentioned thickness of slab central part 2the mean number density of above-mentioned MnS.
(3), according to the heat stamping and shaping body above-mentioned (1) or (2) Suo Shu, wherein, on surface, can further implement galvanizing.
(4), according to the heat stamping and shaping body above-mentioned (3) Suo Shu, wherein, above-mentioned dip galvanized can be hot dip alloyed zinc.
(5), according to the heat stamping and shaping body above-mentioned (1) or (2) Suo Shu, wherein, on surface, can further implement electro-galvanizing.
(6), according to the heat stamping and shaping body above-mentioned (1) or (2) Suo Shu, wherein, on surface, can further implement to aluminize.
(7) manufacture method of the impact briquetting body of a scheme of the present invention, is characterized in that, it comprises following operation: the molten steel of the chemical composition that above-mentioned to having (1) is described casts to make the casting process of steel; The heating process that above-mentioned steel are heated; Use has the equipment of hot rolling of a plurality of frames and above-mentioned steel is implemented to the hot-rolled process of hot rolling; The coiling process after above-mentioned hot-rolled process, above-mentioned steel being batched; Above-mentioned steel are carried out the pickling process of pickling after above-mentioned coiling process; Under the condition of setting up at following formula e with the cold-rolling mill with a plurality of frames, above-mentioned steel are implemented to cold rolling cold rolling process after above-mentioned pickling process; Above-mentioned steel are heated to 700 ℃～850 ℃ and carry out cooling annealing operation after above-mentioned cold rolling process; Above-mentioned steel are carried out the skin-pass operation of skin-pass after above-mentioned annealing operation; With after above-mentioned modified operation, above-mentioned steel are heated to more than 750 ℃ temperature provinces and carry out forming process, with more than 10 ℃/sec speed of cooling, are cooled to the hot stamping operation of 20 ℃～300 ℃ with above-mentioned temperature province with more than 5 ℃/sec heat-up rates.
1.5×r1/r+1.2×r2/r+r3/r＞1 (e)
In formula, by i be set as 1,2 or the riYi unit of 3 o'clock be that % is illustrated in above-mentioned cold rolling process in above-mentioned a plurality of frames the cold rolling rate of independent target by the frame of upstream number i section, r be take unit and is represented the total cold rolling rate of the target of above-mentioned cold rolling process as %.
(8) according to the manufacture method of the heat stamping and shaping body above-mentioned (7) Suo Shu, wherein, when the coiling temperature in above-mentioned coiling process being take to unit as ℃ being expressed as CT and the C content of above-mentioned steel, Mn content, Si content and Mo content being take to unit when quality % is expressed as [C], [Mn], [Si] and [Mo], can set up following formula f.
560-474×[C]-90×[Mn]-20×[Cr]-20×[Mo]＜CT＜830-270×[C]-90×[Mn]-70×[Cr]-80×[Mo] (f)
(9) according to the manufacture method of the heat stamping and shaping body above-mentioned (7) or (8) Suo Shu, wherein, when the Heating temperature in above-mentioned heating process being take to unit as ℃ being set as T and time inside furnace being take to unit as minute being set as t, the Mn content of above-mentioned steel and S content being take to unit when quality % is expressed as [Mn] and [S], can set up following formula g.
T×ln(t)/(1.7×[Mn]+[S])＞1500 (g)
(10) according to the manufacture method of the heat stamping and shaping body described in any one in above-mentioned (7)～(9), it can further have the galvanizing operation of above-mentioned steel being implemented galvanizing between above-mentioned annealing operation and above-mentioned skin-pass operation.
(11), according to the manufacture method of the heat stamping and shaping body above-mentioned (10) Suo Shu, it can further have the Alloying Treatment operation of above-mentioned steel being implemented Alloying Treatment between above-mentioned galvanizing operation and above-mentioned skin-pass operation.
(12) according to the manufacture method of the heat stamping and shaping body described in any one in above-mentioned (7)～(9), it can further have the electro-galvanizing operation of above-mentioned steel being implemented electro-galvanizing between above-mentioned skin-pass operation and above-mentioned hot stamping operation.
(13), according to the manufacture method of the heat stamping and shaping body described in any one in above-mentioned (7)～(9), it can further have between above-mentioned annealing operation and above-mentioned skin-pass operation implements the operation of aluminizing of aluminizing to above-mentioned steel.
Invention effect
According to the present invention, because making the pass of C content, Mn content and Si content is suitable relation, and in the formed body after hot stamping, making to take the martensitic hardness that nano-hardness tester records is suitable hardness, can access thus the heat stamping and shaping body with good hole expandability.
Accompanying drawing explanation
Fig. 1 means the chart of the relation between (5 * [Si]+[Mn])/[C] and TS * λ.
Fig. 2 A means the chart of the basis of formula b, formula c, and it means the H2/H1 of heat stamping and shaping body and the chart of the relation between σ HM.
Fig. 2 B means the chart of the basis of formula c, and it means the chart of the relation between σ HM and TS * λ.
Fig. 3 means the chart of the n2/n1 of hot stamping front and back and the basis of the relation between TS * λ and expression d.
Fig. 4 means the chart of the basis of relation between 1.5 * r1/r+1.2 * r2/r+r3/r and H2/H1 and expression e.
Fig. 5 A means the chart of the relation between formula f and martensite minute rate.
Fig. 5 B means the chart of the relation between formula f and perlite minute rate.
Fig. 6 means the chart of the basis of relation between T * ln (t)/(1.7 * [Mn]+[S]) and TS * λ and expression g.
Fig. 7 is the stereographic map of the heat stamping and shaping body that uses in embodiment.
Fig. 8 means the schema of manufacture method of the heat stamping and shaping body of an embodiment of the invention.
Embodiment
As mentioned above, the relation of Si, Mn and C content being set as to suitable relation and the martensitic hardness at regulation position is set as to suitable hardness is important for the formability (hole expandability) that improves heat stamping and shaping body.Up to now, be not conceived to the formability of heat stamping and shaping body and the relation between martensitic hardness and carried out research.
Below, embodiments of the present invention are elaborated.
First, restriction reason to the chemical composition of the cold-rolled steel sheet for hot stamping using in the heat stamping and shaping body of an embodiment of the invention (be sometimes referred to as the heat stamping and shaping body of present embodiment or referred to as heat stamping and shaping body) (comprise and carried out situation zinc-plated or that aluminize, be sometimes referred to as the cold-rolled steel sheet of present embodiment or referred to as hot stamping cold-rolled steel sheet) describes.Below, the unit of the content of each composition " % " refers to " quality % ".In addition, due in hot stamping, the component content of the chemical composition of steel plate does not change, so at cold-rolled steel sheet and having used in the heat stamping and shaping body of this cold-rolled steel sheet, chemical composition is identical.
C: surpass 0.150% and be below 0.300%
For the intensity that C improves steel for reinforced ferrite phase and martensitic phase, it is important element.Yet, when the content of C is 0.150% when following, can not fully obtain martensitic stucture, cannot fully improve intensity.And when surpassing 0.300%, the reduction of extensibility, hole expandability is large.Therefore, the scope of C content is set as surpass 0.150% and be below 0.300%.
Si：0.010％～1.000％
Si suppressing the generation of harmful carbide, to obtain take on complex tissue that ferrite and martensite are main body be important element.But when Si content surpasses 1.000%, not only extensibility or hole expandability reduce, and chemical convertibility also reduces.Therefore, the content of Si is set as below 1.000%.In addition, Si adds for deoxidation, and when the content of Si is less than 0.010%, deoxidation effect is insufficient.Therefore, the content of Si is set as more than 0.010%.
Al：0.010％～0.050％
Al is important element as reductor.In order to obtain the effect of deoxidation, the content of Al is set as more than 0.010%.Even and exceedingly add Al, above-mentioned effect is also saturated, can make on the contrary steel embrittlement, thereby TS * λ is reduced.Therefore, the content of Al is set as to 0.010%～0.050%.
Mn：1.50％～2.70％
Mn is for improving that hardenability is strengthened steel and the element of overstating and wanting.Yet, when the content of Mn is less than 1.50%, cannot fully improve intensity.And when the content of Mn surpasses 2.70%, it is superfluous that hardenability becomes, extensibility, hole expandability reduce.Therefore, the content of Mn is set as to 1.50%～2.70%.In the situation that requiring of stretching is high, preferably the content of Mn is set as below 2.00%.
P：0.001％～0.060％
When P content is many, it makes local elongation rate and weldability deteriorated to grain boundary segregation.Therefore, the content of P is set as below 0.060%.Although wish that P content is few, the cost when making P reduction can cause refining terrifically rises, and therefore preferably the content of P is set as more than 0.001%.
S：0.001％～0.010％
S forms MnS and makes obviously deteriorated element of local elongation rate and weldability.Therefore, using 0.010% upper limit as content.In addition, although wish that S content is few, from the problem of refining cost, consider, preferably using 0.001% lower limit as S content.
N：0.0005％～0.0100％
N is for AlN etc. is separated out and be important element for crystal grain miniaturization.But, when the content of N surpasses 0.0100%, can remaining solid solution N (solid solution nitrogen) and extensibility and hole expandability are reduced.Therefore, the content of N is set as below 0.0100%.In addition, although wish that N content is few, the problem of the cost during from refining considers, preferably usings 0.0005% lower limit as N content.
The cold-rolled steel sheet of present embodiment with the iron that comprises above element, remainder and inevitably impurity consist of basis, but sometimes in order to improve intensity and control sulfide or the shape of oxide compound etc., can also contain according to the content below the upper limit described later the element nb that used, Ti, V, Mo, Cr, Ca, REM (Rare Earth Metal: more than at least one rare earth element), in Cu, Ni, B all the time.These chemical elements might not contain in steel plate, thus its content under be limited to 0%.
Nb, Ti, V make fine Carbonitride Precipitation strengthen the element of steel.In addition, Mo, Cr improve the element that hardenability is strengthened steel.In order to obtain these effects, more than preferably containing Nb:0.001%, more than Ti:0.001%, more than V:0.001%, more than Mo:0.01%, more than Cr:0.01%.But, even contain Nb: surpass 0.050%, Ti: surpass 0.100%, V: surpass 0.100%, Mo: surpass 0.50%, Cr: surpass 0.50%, the effect that intensity rises also can be saturated, but also can cause the reduction of extensibility and hole expandability.Therefore, using respectively 0.050%, 0.100%, 0.100%, 0.50%, 0.50% upper limit as Nb, Ti, V, Mo, Cr.
Ca controls the shape of sulfide and oxide compound, thereby local elongation rate and hole expandability are improved.In order to obtain this effect, preferably contain more than 0.0005%.Therefore but excessive interpolation can cause processibility deteriorated, using 0.0050% upper limit as Ca content.
REM (rare earth element) and Ca are same, control the shape of sulfide and oxide compound, thereby local elongation rate and hole expandability are improved.In order to obtain this effect, preferably contain more than 0.0005%.Therefore but excessive interpolation can make processibility deteriorated, using 0.0050% upper limit as REM content.
Steel can also be further contains above-mentioned element with the scope of Cu:0.01%～1.00%, Ni:0.01%～1.00%, B:0.0005%～0.0020%.These elements also can make hardenability improve the intensity of steel.Yet, in order to obtain this effect, more than preferably containing Cu:0.01%, more than Ni:0.01%, more than B:0.0005%.When above-mentioned scope is following, the effect of strengthening steel is little.Even and add Cu: surpass 1.00%, Ni: surpass 1.00%, B: surpass 0.0020%, the effect that intensity rises also can be saturated, and extensibility and hole expandability can reduce.Therefore, using respectively 1.00%, 1.00%, 0.0020% upper limit as Cu content, Ni content and B content.
In the situation that containing B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca, REM, contain more than one.The remainder of steel comprises Fe and inevitable impurity.As inevitable impurity, so long as the scope of not damaging characteristic just, can further contain the element (such as Sn, As etc.) except above-mentioned.Content at B, Mo, Cr, V, Ti, Nb, Ni, Cu, Ca, REM is prescribed a time limit down lower than above-mentioned, as inevitable impurity, processes.
In addition, heat stamping and shaping body for present embodiment, as shown in Figure 1, when C content (quality %), Si content (quality %) and Mn content (quality %) are expressed as to [C], [Si] and [Mn], the relation of setting up following formula a is important for obtaining enough hole expandability.
(5×[Si]+[Mn])/[C]＞10 (a)
If the value of (5 * [Si]+[Mn])/[C] is below 10, TS * λ, lower than 50000MPa%, cannot obtain enough hole expandability.This be because, if C amount is high, the much higher hard of hard phase, thereby become the large and value difference of λ with the difference of the hardness of soft phase; And, if Si amount or Mn measure TS step-down at least.Therefore, each element need to be set as to above-mentioned scope, and need further to control the balance of its content.With regard to the value of (5 * [Si]+[Mn])/[C], as mentioned above, owing to also not changing after hot stamping, so preferably just meet when cold-rolled steel sheet is manufactured.Yet, even if meet (5 * [Si]+[Mn])/[C] > 10, in the situation that H2/H1 described later, σ HM do not satisfy condition, also can not get enough hole expandability.In Fig. 1, after hot stamping, represent heat stamping and shaping body, before hot stamping, represent hot stamping cold-rolled steel sheet.
As a rule, have using arrange formability (hole expandability) in ferrite and the cold-rolled steel sheet of martensite as the metal structure of main body be ferrite, not equal to be martensite.The relation that inventors of the present invention are conceived between the formabilities such as martensitic hardness and extensibility, hole expandability conducts in-depth research.Consequently, find: as shown in Fig. 2 A, Fig. 2 B, with regard to the heat stamping and shaping of present embodiment, if the martensitic Hardness Distribution of the martensitic hardness ratio of thickness of slab skin section and thickness of slab central part (hardness poor) and thickness of slab central part is the state of regulation, the good forming ability such as extensibility and hole expandability.In addition, find: with regard to cold-rolled steel sheet is used in the hot stamping of the heat stamping and shaping for present embodiment, if the state that above-mentioned hardness ratio, Hardness Distribution are regulation, even if in heat stamping and shaping body, it is also roughly maintained, the good forming abilities such as extensibility, hole expandability.This it is believed that it is because the heat stamping and shaping body after on hot stamping also affects very large even if hot stamping is by the martensitic Hardness Distribution producing in cold-rolled steel sheet.Particularly, it is believed that this be because, even if be enriched in the alloying element of thickness of slab central part, carried out hot stamping, also keep being enriched in the state of central part.; for cold-rolled steel sheet for hot stamping; in the large situation of the martensitic difference of hardness of thickness of slab skin section and thickness of slab central part, or in the situation that the dispersion value of the martensite hardness at thickness of slab central part place is large, it in heat stamping and shaping body, is all when dispersion value of same hardness.In addition, in Fig. 2 A, Fig. 2 B, after hot stamping, represent heat stamping and shaping body, before hot stamping, represent hot stamping cold-rolled steel sheet.
Inventors of the present invention also find: the martensitic measurement of hardness recording with the multiplying power of 1000 times about the nano-hardness tester with HYSITRON company, when following formula b and formula c set up, the formability of heat stamping and shaping body improves.Here, " H1 " for the top layer from heat stamping and shaping body to thickness of slab direction 200 μ m with interior be the martensitic hardness of thickness of slab skin section." H2 " for the thickness of slab central part of heat stamping and shaping body be in thickness of slab direction from thickness of slab center to ± 100 μ m with interior martensitic hardness.The dispersion value of the martensitic hardness in the thickness of slab direction that is present in thickness of slab central part place that " σ HM " is heat stamping and shaping body in the scope of 200 μ m.Measure respectively 300 points.In the thickness of slab direction at thickness of slab central part place, the scope of 200 μ m is of a size of the scope of 200 μ m for thickness of slab direction centered by thickness of slab center.
H2/H1＜1.10 (b)
σHM＜20 (c)
In addition, dispersion value is obtained by following formula h here, and it is for representing the value of martensitic Hardness Distribution.
Mathematical expression 1
&sigma;HM = 1 n &Sigma; i = 1 n ( x ave - x i ) 2 - - - ( h )
X avefor the mean value of the martensite hardness that records, X irepresent i martensitic hardness.
Fig. 2 A represents heat stamping and shaping body and the martensite hardness of skin section of cold-rolled steel sheet and the ratio of the martensite hardness of thickness of slab central part for hot stamping.In addition, Fig. 2 B represents the dispersion value of the martensitic hardness in the scope of be present in from thickness of slab center the thickness of slab direction ± 100 μ m of cold-rolled steel sheet for heat stamping and shaping body and hot stamping in the lump.From Fig. 2 A and Fig. 2 B, the hardness ratio of the cold-rolled steel sheet before hot stamping and the hardness ratio of the cold-rolled steel sheet after hot stamping are basic identical.In addition, in cold-rolled steel sheet and the cold-rolled steel sheet after hot stamping before hot stamping, the dispersion value of the martensitic hardness of thickness of slab central part is also basic identical.
For heat stamping and shaping body, the value of H2/H1 is more than 1.10 to represent that the martensitic hardness of thickness of slab central part is the more than 1.10 times of martensitic hardness of thickness of slab skin section.That is the much higher hard that, represents thickness of slab central part.As known in Fig. 2 A, if H2/H1 is more than 1.10, σ HM is more than 20.Now, TS * λ < 50000MPa%, is in heat stamping and shaping body, also to can not get enough formabilities after quenching.The lower limit of H2/H1 only otherwise carry out special thermal treatment, situation about being equal to for thickness of slab central part and thickness of slab skin section in theory, but in fact in the production process of consideration productivity, for example, be 1.005 left and right.
The dispersion value σ HM of heat stamping and shaping body is more than 20 represent martensitic hardness inhomogeneous large, has partly the part of much higher hard.Now, TS * λ < 50000MPa%.That is, in heat stamping and shaping body, can not get enough formabilities.
Then, the metal structure for the heat stamping and shaping body of present embodiment describes.The martensite area occupation ratio of the heat stamping and shaping body of present embodiment is more than 80%.If martensite area occupation ratio is less than 80%, can not get the desired enough intensity of heat stamping and shaping body (for example 1.5GPa) in recent years.Therefore, martensite area occupation ratio is set as more than 80%.Whole or the integral part of the metal structure of heat stamping and shaping body is occupied by martensite, but sometimes also can contain in addition with area occupation ratio, counts 0～10% perlite, with volume fraction, counts 0～5% retained austenite, with area occupation ratio, count 0～20% ferrite and count more than 0% and lower than more than one in 20% bainite with area occupation ratio.Ferrite exists 0%～20% sometimes according to hot stamping condition, the scope of this degree if, and the intensity after hot stamping is no problem.If remaining in metal structure, have a retained austenite, secondary processing brittleness and delayed fracture characteristic easily reduce.Therefore, preferably in fact not containing retained austenite, but inevitably also can contain with volume fraction and count the retained austenite below 5%.Because perlite is hard and crisp tissue, thus preferably do not contain, but also can allow inevitably and contain 10% in area occupation ratio.Bainite is to can be used as the tissue that residual tissue produces, and from intensity and formability, considers, it is middle tissue, also can not contain, but allows and be less than 20% in area occupation ratio maximum.In the present embodiment, with regard to metal structure, ferrite, bainite, perlite carry out the etching of nitric acid ethanol, and martensite carries out Lepera etching, all 1/4 use opticmicroscope of thickness of slab are observed with 1000 times.For retained austenite, steel plate is ground to behind thickness of slab 1/4 position, by X-ray diffraction device, measure volume fraction.
Then, the hot stamping for the heat stamping and shaping body for present embodiment describes with the preferable alloy tissue of cold-rolled steel sheet.The metal structure of heat stamping and shaping body is subject to the impact of the metal structure of cold-rolled steel sheet for hot stamping.Therefore,, by controlling the metal structure of cold-rolled steel sheet for hot stamping, easily in heat stamping and shaping body, obtain above-mentioned metal structure.The ferrite area occupation ratio of the cold-rolled steel sheet of present embodiment is preferably 40%～90%.If ferrite area occupation ratio is lower than 40%, intensity starts just to become too high from hot stamping, thereby the shape of heat stamping and shaping body worsens sometimes, cuts off the difficulty that becomes.Therefore, preferably the ferrite area occupation ratio before hot stamping is set as more than 40%.In addition, in the cold-rolled steel sheet of present embodiment, because the content of alloying element is many, so be difficult to make ferrite area occupation ratio to surpass 90%.Except ferrite, in metal structure, also contain martensite, its area occupation ratio is preferably 10～60%.Ferrite area occupation ratio and martensite area occupation ratio sum are preferably more than 60% before hot stamping.In metal structure, also can further contain more than one in perlite, bainite and retained austenite.Just, if remaining in metal structure, have a retained austenite, secondary processing brittleness and delayed fracture characteristic easily reduce, therefore preferably in fact containing retained austenite.Yet, inevitably also can contain with volume fraction and count the retained austenite below 5%.Because perlite is hard and crisp tissue, thus preferably do not contain, but can allow inevitably and contain 10% in area occupation ratio.As residual tissue, bainite and above-mentioned reason are same, can allow in area occupation ratio and contain and be less than 20% at most.Cold-rolled steel sheet before metal structure and hot stamping is same, by the etching of nitric acid ethanol, observes ferrite, bainite, perlite, by Lepera etching, observes martensite.In either case, all use opticmicroscope to observe 1/4 of thickness of slab with 1000 times.For retained austenite, steel plate is ground to behind thickness of slab 1/4 position, with X-ray diffraction device, measure volume fraction.
In addition, in the heat stamping and shaping body of present embodiment, martensitic hardness (penetration hardness (GPa or N/mm that regulation records with the multiplying power of 1000 times with nano-hardness tester 2) or be converted into from penetration hardness the value that Vickers' hardness (HV) forms).Due in common Vickers hardnes test, formed impression is larger than martensite.So, although can obtain the hardness of the broad perspectives of martensite and tissue around (ferrite etc.) thereof, can not get itself hardness of martensite.Itself hardness of martensite is very large on the impact of the formability such as hole expandability, therefore only with Vickers' hardness, is difficult to evaluate fully formability.On the other hand, in the heat stamping and shaping body of present embodiment, the hardness ratio of the martensitic hardness recording with nano-hardness tester, dispersion state are controlled to suitable scope, therefore can obtain very good formability.
In the position of the thickness of slab 1/4 of heat stamping and shaping body, (position of 1/4 the degree of depth from surface to thickness of slab) and thickness of slab central part are observed MnS.Consequently, known: diameter of equivalent circle is that the area occupation ratio of the MnS of 0.1 μ m～10 μ m is below 0.01%, and as shown in Figure 3, it is preferred well and stably obtaining on TS * λ >=50000MPa% that following formula d sets up.
n2/n1＜1.5 (d)
In formula, n1 is that the diameter of equivalent circle of per unit area of 1/4 of the thickness of slab of heat stamping and shaping body is individual number density (mean number density) (individual/10000 μ m of the MnS of 0.1 μ m～10 μ m 2), n2 is that the diameter of equivalent circle of per unit area of the thickness of slab central part of heat stamping and shaping body is individual number density (mean number density) (individual/10000 μ m of the MnS of 0.1 μ m～10 μ m 2).
As the MnS of 0.1 μ m～10 μ m being set as to area occupation ratio, be 0.01% when following, the reason that formability improves it is believed that it is because when implementing drifiting test, be MnS more than 0.1 μ m if there is diameter of equivalent circle, stress concentration is around it, so easily crack.It is because the concentrated impact of its counter stress is little that the MnS that diameter of equivalent circle is not less than to 0.1 μ m counts; And it is excessive to surpass 10 μ m, be just not suitable for processing originally.In addition,, if the area occupation ratio of the MnS of 0.1 μ m～10 μ m surpasses 0.01%, the fine crackle being produced by stress concentration is easily propagated.Therefore, hole expandability can reduce sometimes.In addition, the lower limit of the area occupation ratio of MnS does not have special stipulation, but from content, the desulfurization processing power of restriction, Mn or the S of measuring method described later and multiplying power, visual field, consider, being set as being less than 0.0001% has impact for productivity, cost, so more than 0.0001% be appropriate.
If diameter of equivalent circle is that the area occupation ratio of the MnS of 0.1 μ m～10 μ m surpasses 0.01% in heat stamping and shaping body, as mentioned above, due to stress concentration, formability easily reduces.On the other hand, in heat stamping and shaping body, the value of n2/n1 is that the individual number density of MnS that more than 1.5 represents the thickness of slab central part of heat stamping and shaping body is the more than 1.5 times of individual number density of MnS of 1/4 of the thickness of slab of heat stamping and shaping body.Now, due to the segregation of the MnS of thickness of slab central part and formability easily reduces.In the present embodiment, the diameter of equivalent circle of MnS and individual number density are used the Fe-SEM (field emission scanning electron microscope, Field Emission Scanning Electron Microscope) of JEOL company to measure.Multiplying power is 1000 times, and the mensuration area of 1 visual field is 0.12 * 0.09mm 2(=10800 μ m 2≈ 10000 μ m 2).In the position of 1/4 degree of depth from surface to thickness of slab (1/4 of thickness of slab), observe ten visual fields, at thickness of slab central part, observe ten visual fields.The area occupation ratio of MnS is used particle analysis software to calculate.In the present embodiment, not only to heat stamping and shaping body, and to hot stamping, with cold-rolled steel sheet, observe MnS.Consequently, known: before hot stamping, (hot stamping cold-rolled steel sheet) be not even if the form of the MnS producing changes at heat stamping and shaping body (after hot stamping) yet.Fig. 3 means the n2/n1 of heat stamping and shaping body and the figure of the relation between TS * λ, and with 1/4 of the thickness of slab of cold-rolled steel sheet, uses with heat stamping and shaping body identical index evaluation to represent with the measurement result of the individual number density of the MnS at thickness of slab central part place to hot stamping.In Fig. 3, after hot stamping, represent heat stamping and shaping body, before hot stamping, represent hot stamping cold-rolled steel sheet.As can be seen from Figure 3, the n2/n1 of cold-rolled steel sheet and heat stamping and shaping body for hot stamping (1/4 of thickness of slab with thickness of slab central part MnS ratio) is basically identical.This is because under the Heating temperature of hot stamping, the form of MnS does not change.
The heat stamping and shaping body of present embodiment obtains by following method: the cold-rolled steel sheet of present embodiment is for example heated to 750 ℃～1000 ℃ with the heat-up rate of 5 ℃/sec～500 ℃/sec, during 1 second～120 seconds, carry out moulding (processing), and be cooled to the temperature province of 20 ℃～300 ℃ with the speed of cooling of 10 ℃/sec～1000 ℃/sec.Resulting heat stamping and shaping body has 1500MPa to the tensile strength of 2200MPa, particularly has 1800MPa and can obtain the effect of significant formability raising to the high tensile steel plate of 2000MPa left and right.
If the heat stamping and shaping body of present embodiment has been implemented to zinc, for example plate galvanizing, alloyed hot-dip zinc-coated, electro-galvanizing or aluminize, be preferred on antirust.In the situation that heat stamping and shaping body is implemented to plating, under the hot stamping condition above-mentioned, coating does not change, so as long as hot stamping is implemented to plating with cold-rolled steel sheet.Even heat stamping and shaping body has been implemented to these plating, also can not damage the effect of present embodiment.These plating can be implemented by known method.
Below, for the cold-rolled steel sheet of present embodiment and by this cold-rolled steel sheet being carried out to the manufacture method of the heat stamping and shaping body of the present embodiment that hot stamping obtains, describe.
When manufacturing the cold-rolled steel sheet of present embodiment, as common condition, by casting continuously after converter to make it have the molten steel that the mode melting of above-mentioned chemical composition forms, make slab.During continuous casting, if casting speed is fast, the precipitate such as Ti is too fine.And if slow, not only produce rate variance, and above-mentioned precipitate coarsening, thereby population tails off, and becomes sometimes the form of other characteristics such as uncontrollable delayed fracture.Therefore, preferably casting speed is set as to 1.0m/ minute～2.5m/ minute.
Slab after melting and casting can be directly for hot rolling.Or, in the situation that being cooled to lower than 1100 ℃, can in continuous tunnel furnace etc., reheat 1100 ℃～1300 ℃, then for hot rolling.In the situation that the temperature of slab during hot rolling is the temperature lower than 1100 ℃, in hot rolling, be difficult to guarantee finishing temperature, become the reason that extensibility reduces.In addition, in having added the steel plate of Ti, Nb, the dissolving of precipitate during heating is insufficient, therefore becomes the reason of strength decreased.And when the temperature of slab surpasses 1300 ℃, it is large that the generation of oxide skin becomes, thereby likely the surface texture of steel plate can not be fabricated to good surface texture.
In addition, in order to reduce the area occupation ratio of MnS, when the Mn content (quality %) of steel, S content (quality %) are expressed as to [Mn], [S], as shown in Figure 6, implement the process furnace before hot rolling temperature T (℃), time inside furnace t (minute), [Mn] and [S] be preferably to make and state formula g.
T×ln(t)/(1.7×[Mn]+[S])＞1500 (g)
If the value of T * ln (t)/(1.7[Mn]+[S]) is below 1500, the area occupation ratio of MnS becomes large sometimes, and the number of MnS of 1/4 of the thickness of slab of MnS becomes greatly with the difference of the number of the MnS of thickness of slab central part.In addition, the temperature of implementing the process furnace before hot rolling refers to that process furnace goes out side and extracts temperature out, and time inside furnace refers to and slab inserted to hot-rolling heating furnace till the time of extracting out.With regard to MnS, owing to not changing by rolling or hot stamping as mentioned above, so meet formula g just when the heating of slab.In addition, above-mentioned ln represents natural logarithm.
Then,, according to ordinary method, carry out hot rolling.Now, preferably finishing temperature (hot rolling end temp) is set as to Ar3 temperature～970 ℃, slab is carried out to hot rolling.When finishing temperature is during lower than Ar3 temperature, become the two-phase region rolling of ferrite (α) and austenite (γ), likely can cause the reduction of extensibility.And when surpassing 970 ℃, austenite particle diameter becomes thick, thereby a ferrite minute rate diminishes, and extensibility likely reduces.
Ar3 temperature is measured the variation of the length of accompanying temperature variant test film and is inferred by its flex point by carrying out Formastor (phase transformation instrument) test.
After hot rolling, steel is carried out cooling with the average cooling rate of 20 ℃/sec～500 ℃/sec, with the coiling temperature CT ℃ stipulating, batch.In speed of cooling lower than 20 ℃/sec in the situation that, owing to easily becoming the perlite of the reason of extensibility reduction, so not preferred.
On the other hand, the upper limit of speed of cooling does not have special stipulation, and the viewpoint of slave unit specification is considered, preferably the upper limit of speed of cooling is set as to 500 ℃/sec of left and right, but is not limited to this.
After batching, carry out pickling, and carry out cold rolling (cold rolling).Now, as shown in Figure 4, in order to be met the scope of above-mentioned formula b, under the condition of setting up at following formula e, carry out cold rolling.By carrying out the rolling and further meeting annealing described later, the condition such as cooling, as the cold-rolled steel sheet before hot stamping, can obtain TS * λ >=50000MPa% thus, and then can guarantee TS * λ >=50000MPa% in having used the heat stamping and shaping body of this cold-rolled steel sheet.In addition, the tandem roller mill that cold rolling preferred use is following, it is by many roller mills with straight line configuration, and continuous rolling, obtains the thickness of stipulating thus in one direction.
1.5×r1/r+1.2×r2/r+r3/r＞1.0 (e)
Wherein, " ri (i=1,2 and 3) " be above-mentioned cold rolling in by the cold rolling rate of independent target (%) of the frame of upstream number i (i=1,2 and 3) section, r is the total cold rolling rate (%) of above-mentioned cold rolling target.
Total rolling rate is so-called accumulation rolling rate, usings the entrance thickness of slab of initial frame as benchmark, and it is that accumulation draught (the outlet thickness of slab after the entrance thickness of slab before initial passage and final passage poor) is with respect to the percentage of this benchmark.
If carry out cold rollingly under the condition of setting up at above-mentioned formula e, even at the large perlite of cold rolling front existence, also can middle perlite be cut apart fully cold rolling.Consequently, by the annealing of carrying out after cold rolling, can make perlite disappear, or pearlitic area occupation ratio can be suppressed to inferior limit.Therefore, be easily met the tissue of formula b and formula c.And in the invalid situation of formula e, the cold rolling rate of the frame of upstream side is insufficient, easy residual large perlite.Consequently, in annealing operation, can not generate the martensite with desirable form.
In addition, inventors of the present invention find: in the cold-rolled steel sheet after the rolling of having carried out meeting formula e, even the form of the martensitic stucture obtaining after annealing after carry out hot stamping, also can maintain essentially identical state, for extensibility and the hole expandability of heat stamping and shaping body, be favourable.The hot stamping of present embodiment is with cold-rolled steel sheet in the situation that being heated to austenite region by hot stamping, and comprising martensitic hard phase becomes the austenite structure that C concentration is high, and ferritic phase becomes the austenite structure that C concentration is low.Afterwards, if carry out coolingly, austenite becomes mutually and comprises martensitic hard phase.That is, if meet the hot stamping of such (above-mentioned H2/H1 is that the scope of regulation is such) the martensite hardness of formula e to having, with steel plate, carry out hot stamping,, after hot stamping, above-mentioned H2/H1 is also the scope of regulation, and the formability after hot stamping is excellent.
In the present embodiment, r, r1, r2, r3 are the cold rolling rate of target.Conventionally, the cold rolling rate of target and the cold rolling rate of actual achievement are controlled as essentially identical value and carry out cold rolling.Preferably do not make the cold rolling rate of actual achievement too depart to carry out cold rolling with respect to the cold rolling rate of target.In target rolling rate and actual rolling rate, depart from large in the situation that, if can recognize the cold rolling rate of judgement actual achievement, meet above-mentioned formula e, can implement the present invention.Actual cold rolling rate is preferably in cold rolling rate ± 10% of target.
After cold rolling, anneal.By annealing, make to produce recrystallize in steel plate, produce desirable martensite.About annealing temperature, preferably by ordinary method, be heated to the temperature range of 700～850 ℃, then anneal, and be cooled to 20 ℃ or carry out the surface-treated temperature such as galvanizing till.By annealing in this temperature range, desirable area occupation ratio can be guaranteed respectively in ferrite and martensite, and ferrite area occupation ratio and martensite area occupation ratio sum be more than 60%, so TS * λ improves.
Condition except annealing temperature does not have special stipulation, in order to obtain reliably the tissue of regulation, under the hold-time of 700 ℃～850 ℃ preferably keeps, be limited to 1 second above and do not hinder the scope of productivity, for example, about 10 minutes.Heat-up rate preferably more than 1 ℃/sec and the capacity of equipment upper limit for example 1000 ℃/sec following suitably determine, speed of cooling preferably more than 1 ℃/sec and the capacity of equipment upper limit for example 500 ℃/sec following suitably definite.Skin-pass is undertaken just by ordinary method.The extensibility of skin-pass is generally 0.2～5% left and right, preferably for fear of yield-point stretching, can proofread and correct the degree of steel plate shape.
As the condition being more preferably of the present invention, when the C content (quality %) of steel, Mn content (quality %), Si content (quality %) and Mo content (quality %) are expressed as to [C], [Mn], [Si] and [Mo], the coiling temperature CT in above-mentioned coiling process is preferably to make and states formula f.
560-474×[C]-90×[Mn]-20×[Cr]-20×[Mo]＜CT＜830-270×[C]-90×[Mn]-70×[Cr]-80×[Mo] (f)
As shown in Figure 5A, if coiling temperature CT is lower than 560-474 * [C]-90 * [Mn]-20 * [Cr]-20 * [Mo],, CT-560-474 * [C]-90 * [Mn]-20 * [Cr]-20 * [Mo] is less than 0, martensite generates superfluously, it is really up to the mark that steel plate becomes, the cold rolling difficulty that becomes sometimes of carrying out afterwards.And as shown in Figure 5 B, if coiling temperature CT surpasses 830-270 * [C]-90 * [Mn]-70 * [Cr]-80 * [Mo], that is, 830-270 * [C]-90 * [Mn]-70 * [Cr]-80 * [Mo] surpasses 0, easily generate and comprise ferrite and pearlitic banded structure.In addition, at thickness of slab central part, pearlitic ratio easily raises.Therefore, after annealing operation in the consistence of the martensitic distribution that generates reduce, above-mentioned formula b is difficult to set up.In addition, sometimes be also difficult to generate the martensite of abundant amount.
If meet formula f, as mentioned above, before hot stamping, ferritic phase and hard phase become desirable distributional pattern.In addition, now, after heating with hot stamping, C etc. are diffusion equably easily.Therefore, the distributional pattern of the martensitic hardness of heat stamping and shaping body approaches desirable.If can meet formula f and guarantee more reliably above-mentioned metal structure, the formability of heat stamping and shaping body becomes excellent.
In addition, take and improve antirust ability as object, also preferably there is the galvanizing operation of implementing galvanizing between above-mentioned annealing operation and skin-pass operation, on the surface of cold-rolled steel sheet, implement galvanizing.In addition, alloyed hot-dip zinc-coated for galvanizing alloying is obtained, also preferably there is the Alloying Treatment operation of implementing Alloying Treatment between galvanizing operation and skin-pass operation.In the situation that implementing Alloying Treatment, the processing that also can further implement to make alloyed hot-dip zinc-coated surface and water vapour etc. for being oxidized the material of coating surface and contacting, oxide film to be thickened.
Except galvanizing operation, Alloying Treatment operation, also preferably there is the electro-galvanizing operation of for example surface of cold-rolled steel plate being implemented electro-galvanizing after skin-pass operation.In addition, also preferably replace galvanizing, there is the operation of aluminizing that enforcement is aluminized between annealing operation and skin-pass operation, surface of cold-rolled steel plate is implemented to aluminize.Aluminize and be conventionally preferably hot dip aluminum plating.
After a series of processing like this, resulting hot stamping is carried out to hot stamping with cold-rolled steel sheet, make heat stamping and shaping body.The operation of hot stamping is for example preferably carried out according to following condition.First, with 5 ℃/sec～500 ℃/sec of heat-up rates, be heated to 750 ℃～1000 ℃.After heating, during 1 second～120 seconds, process (moulding).In order to make high strength, Heating temperature preferably surpasses Ac3 point.Ac3 point is inferred by the flex point of the length of test film by carrying out Formastor test.
Then, preference is as being cooled to 20 ℃～300 ℃ with 10 ℃/sec～1000 ℃/sec of speed of cooling.In Heating temperature, during lower than 750 ℃, in heat stamping and shaping body, martensite divides rate inadequate, cannot guarantee intensity.When Heating temperature surpasses 1000 ℃, too softening, and in the situation that surface of steel plate has been implemented plating, particularly implemented in zinc-plated situation, the possibility that have zinc evaporation, disappears, so not preferred.The Heating temperature of therefore, hot stamping operation is preferably 750 ℃～1000 ℃.When heat-up rate is less than 5 ℃/sec, it controls difficulty, and productivity significantly reduces, and therefore preferably with 5 ℃/sec of above heat-up rates, heats.And 500 ℃/sec of the heat-up rate upper limit determine by present situation heating efficiency, but be not limited to this.When speed of cooling is less than 10 ℃/sec, its speed control difficulty, productivity also significantly reduces, and therefore preferably with 10 ℃/sec of above speed of cooling, carries out cooling.The speed of cooling upper limit is not particularly limited, if but consider present situation cooling power, be below 1000 ℃/sec.After heating up, become to type first being processed be set as 1 second～within 120 seconds, be in order to avoid the evaporations such as this zinc the surface of steel plate enforcement galvanizing etc. in the situation that.It is in order to guarantee fully martensite that cooling temperature is set as to 20 ℃ of (normal temperature)～300 ℃, thereby guarantees the intensity after hot stamping.
As from the foregoing, if meet above-mentioned condition, can manufacture following heat stamping and shaping body, the Hardness Distribution in its cold-rolled steel sheet and be organized in hot stamping after be also roughly maintained, guarantee intensity and can access better hole expandability.
In addition the schema (operation S1～S14) of an example that represents, the manufacture method of above-mentioned explanation in Fig. 8.
Embodiment
After the steel of the composition shown in his-and-hers watches 1 casts continuously with casting speed 1.0m/ minute～2.5m/ minute, direct or temporarily cooling, then the condition with table 2 heats slab according to ordinary method with process furnace, with the finishing temperatures of 910～930 ℃, carries out hot rolling, makes hot-rolled steel sheet.Then, this hot-rolled steel sheet is batched with the coiling temperature CT shown in table 2.Afterwards, carry out pickling, thereby remove the oxide skin of surface of steel plate, with the cold rolling thickness of slab 1.2～1.4mm that makes.Now, the mode that becomes the value shown in table 2 with the value of formula e is carried out cold rolling.After cold rolling, with continuous annealing furnace, with the annealing temperature shown in table 3, table 4, anneal.To the further cooling galvanizing of implementing after continuous annealing furnace soaking of a part of steel plate midway, thereby and then to its part after implement Alloying Treatment and implement alloyed hot-dip zinc-coated.In addition, a part of steel plate is implemented electro-galvanizing or aluminized.Skin-pass be take extensibility and is rolled according to ordinary method as 1%.Under this state, gather in order to evaluate the sample of the material of cold-rolled steel sheet etc. for hot stamping, carry out material test etc.Then, in order to obtain the heat stamping and shaping body of form as shown in Figure 7, carry out after heating up with 10 ℃/sec of heat-up rates, keeping 10 seconds with 850 ℃ of Heating temperatures with 100 ℃/sec of hot stampings that are cooled to below 200 ℃ of speed of cooling.Position by Fig. 7 from resulting formed body cuts out sample, carries out material test, structure observation, obtains each individual number density of organizing minute rate, MnS, hardness, tensile strength (TS), extensibility (El), hole expansibility (λ) etc.Its result is illustrated in table 3～table 8.Hole expansibility λ in table 3～table 6 is tried to achieve by following formula i.
λ(％)＝{(d’-d)/d}×100 (i)
D ': aperture when be full of cracks connects thickness of slab
D: the initial diameter in hole
In the kind of the plating in table 5, table 6, CR is the cold-rolled steel sheet without plating, and GI represents to have implemented galvanizing, and GA represents to have implemented alloy galvanizing, and EG represents to have implemented plating, and the electric plating of Al is aluminized.
Content in table 1 " 0 " represents that content is below determination limit.
The G of the judgement in table 2, table 7, table 8, B represent respectively the following meaning.
G: meet the conditional as object.
B: do not meet the conditional as object.
Table 2
From table 1～table 8, if meet important document of the present invention just can be met TS * λ >=50000MPa% use the heat stamping and shaping body of high strength cold rolled steel plate.
Utilizability in industry
According to the present invention, owing to making the pass of C content, Mn content and Si content, it is suitable relation, and make the martensitic hardness recording with nano-hardness tester become suitable hardness, so can provide the intensity of guaranteeing more than 1.5GPa and the heat stamping and shaping body that can obtain good hole expandability.
Nomenclature
S1 melting operation
S2 casting process
S3 heating process
S4 hot-rolled process
S5 coiling process
S6 pickling process
S7 cold rolling process
S8 annealing operation
S9 skin-pass operation
S10 hot stamping operation
S11 galvanizing operation
S12 Alloying Treatment operation
The S13 operation of aluminizing
S14 electro-galvanizing operation

Claims (13)

1. a heat stamping and shaping body, it is characterized in that, it be take quality % and contains C: surpass 0.150% and as below 0.300%, Si:0.010%～1.000%, Mn:1.50%～2.70%, P:0.001%～0.060%, S:0.001%～0.010%, N:0.0005%～0.0100% and Al:0.010%～0.050%
Sometimes optionally contain more than one in B:0.0005%～0.0020%, Mo:0.01%～0.50%, Cr:0.01%～0.50%, V:0.001%～0.100%, Ti:0.001%～0.100%, Nb:0.001%～0.050%, Ni:0.01%～1.00%, Cu:0.01%～1.00%, Ca:0.0005%～0.0050% and REM:0.0005%～0.0050%, remainder comprises Fe and inevitable impurity
When C content, Si content and Mn content being take to unit when quality % is expressed as [C], [Si] and [Mn], set up the relation of following formula a,
Metal structure contains with area occupation ratio counts more than 80% martensite, sometimes also contain in area occupation ratio and count perlite below 10%, with volume fraction, count retained austenite below 5%, with area occupation ratio, count the ferrite below 20% and with area occupation ratio, be less than more than one in 20% bainite
The amassing of tensile strength TS and hole expansibility λ is that TS * λ is more than 50000MPa%,
The described martensitic hardness recording with nano-hardness tester meets following formula b and formula c,
5×[Si]+[Mn])/[C]＞10 (a)
H2/H1＜1.10 (b)
σHM＜20 (c)
In formula, H1 is the described martensitic average hardness of skin section, H2 is for being the described martensitic average hardness of thickness of slab central part from thickness of slab center along the scope of thickness of slab direction ± 100 μ m, and σ HM is the dispersion value that is present in the described martensitic hardness of described thickness of slab central part.
2. heat stamping and shaping body according to claim 1, is characterized in that, the area occupation ratio that is present in diameter of equivalent circle in described metal structure and is the MnS of 0.1 μ m～10 μ m is below 0.01%, sets up following formula d,
n2/n1＜1.5 (d)
In formula, n1 is every 10000 μ m of 1/4 of thickness of slab 2the mean number density of described MnS, n2 is every 10000 μ m of described thickness of slab central part 2the mean number density of described MnS.
3. heat stamping and shaping body according to claim 1 and 2, is characterized in that, has further implemented galvanizing on surface.
4. heat stamping and shaping body according to claim 3, is characterized in that, described dip galvanized comprises hot dip alloyed zinc.
5. heat stamping and shaping body according to claim 1 and 2, is characterized in that, has further implemented electro-galvanizing on surface.
6. heat stamping and shaping body according to claim 1 and 2, is characterized in that, has further implemented to aluminize on surface.
7. a manufacture method for heat stamping and shaping body, is characterized in that, it comprises following operation:
To thering is the molten steel of chemical composition claimed in claim 1, cast to make the casting process of steel;
The heating process that described steel are heated;
Use has the equipment of hot rolling of a plurality of frames and described steel is implemented to the hot-rolled process of hot rolling;
The coiling process after described hot-rolled process, described steel being batched;
Described steel are carried out the pickling process of pickling after described coiling process;
Under the condition of setting up at following formula e with the cold-rolling mill with a plurality of frames, described steel are implemented to cold rolling cold rolling process after described pickling process;
Described steel are heated to 700 ℃～850 ℃ and carry out cooling annealing operation after described cold rolling process;
Described steel are carried out the skin-pass operation of skin-pass after described annealing operation; With
After described modified operation, described steel are heated to more than 750 ℃ temperature provinces and carry out forming process, with more than 10 ℃/sec speed of cooling, are cooled to the hot stamping operation of 20 ℃～300 ℃ with described temperature province with more than 5 ℃/sec heat-up rates,
1.5×r1/r+1.2×r2/r+r3/r＞1 (e)
In formula, by i be set as 1,2 or the riYi unit of 3 o'clock be that % is illustrated in described in described cold rolling process in a plurality of frames the cold rolling rate of independent target by the frame of upstream number i section, r be take unit and is represented the total cold rolling rate of the target of described cold rolling process as %.
8. the manufacture method of heat stamping and shaping body according to claim 7, it is characterized in that, when the coiling temperature in described coiling process being take to unit as ℃ being expressed as CT and the C content of described steel, Mn content, Si content and Mo content being take to unit when quality % is expressed as [C], [Mn], [Si] and [Mo], set up following formula f
560-474×[C]-90×[Mn]-20×[Cr]-20×[Mo]＜CT＜830-270×[C]-90×[Mn]-70×[Cr]-80×[Mo] (f)。
9. according to the manufacture method of the heat stamping and shaping body described in claim 7 or 8, it is characterized in that, when the Heating temperature in described heating process being take to unit as ℃ being set as T and time inside furnace being take to unit as minute being set as t, the Mn content of described steel and S content being take to unit when quality % is expressed as [Mn] and [S], set up following formula g
T×ln(t)/(1.7×[Mn]+[S])＞1500 (g)。
10. according to the manufacture method of the heat stamping and shaping body described in claim 7 or 8, it is characterized in that, it further has the galvanizing operation of described steel being implemented galvanizing between described annealing operation and described skin-pass operation.
The manufacture method of 11. heat stamping and shaping bodies according to claim 10, is characterized in that, it further has the Alloying Treatment operation of described steel being implemented Alloying Treatment between described galvanizing operation and described skin-pass operation.
12. according to the manufacture method of the heat stamping and shaping body described in claim 7 or 8, it is characterized in that, it further has the electro-galvanizing operation of described steel being implemented electro-galvanizing between described skin-pass operation and described hot stamping operation.
13. according to the manufacture method of the heat stamping and shaping body described in claim 7 or 8, it is characterized in that, it further has between described annealing operation and described skin-pass operation implements the operation of aluminizing of aluminizing to described steel.
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